CN111235436B - In-situ synthesized aluminum carbide reinforced aluminum-based composite material and preparation method thereof - Google Patents

In-situ synthesized aluminum carbide reinforced aluminum-based composite material and preparation method thereof Download PDF

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CN111235436B
CN111235436B CN202010045524.8A CN202010045524A CN111235436B CN 111235436 B CN111235436 B CN 111235436B CN 202010045524 A CN202010045524 A CN 202010045524A CN 111235436 B CN111235436 B CN 111235436B
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composite material
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graphene
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高海燕
李敏
张驰
王朦朦
吕海洋
王宇飞
王俊
孙宝德
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Shanghai Jiaotong University
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    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
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    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
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    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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Abstract

The invention provides an in-situ synthesized aluminum carbide reinforced aluminum-based composite material and a preparation method thereof4C3Nano-scale of Al4C3The aluminum alloy is distributed in the composite material in two forms, wherein one form is that two ends of a rod-shaped appearance respectively grow towards the insides of two aluminum crystal grains to nail two adjacent aluminum crystal grains, and the other form is that the rod-shaped appearance is arranged along a grain boundary in the length direction of the rod shape, so that dislocation and grain boundary migration can be effectively prevented. In one aspect of the invention, the Al is in the nanometer scale4C3Effectively pinning the grain boundary migration of the Al matrix, keeping the strength of the Al matrix and simultaneously Al4C3As a hard reinforcing phase, the composite material has higher room temperature strength and high temperature mechanical property due to stress bearing and olorowan effect, and the composite material has wide application prospect in the field of high service temperature conditions such as aerospace and the like.

Description

In-situ synthesized aluminum carbide reinforced aluminum-based composite material and preparation method thereof
Technical Field
The invention relates to the technical field of heat-resistant metal matrix composite materials, in particular to in-situ synthesis of aluminum carbide Al4C3A reinforced aluminum matrix composite material and a preparation method thereof.
Background
The heat-resistant aluminum alloy has high strength and good heat resistance, and is widely applied to the field of aerospace. However, when the working temperature exceeds 200 ℃, the coarsening of the main strengthening phase significantly reduces the mechanical properties, and is difficult to meet the requirements of new-generation aircraft, propellers and other structural components on the use temperature, so the development of aluminum alloy and aluminum-based composite materials with higher room temperature strength, better damage resistance, excellent heat resistance and heat stability becomes one of the current aluminum alloy research hotspots.
Through search, documents "interface reaction induced effective load transfer in raw-layer graphene reactions for Al matrix Composites for high-performance Composites, Composites Part B, 2019,167" report that the graphene reinforced aluminum matrix Composites have excellent properties such as high strength and high modulus, and the interface is subjected to appropriate amount of reaction to generate Al after heat treatment4C3The method is favorable for the interface bonding strength of the graphene and the Al matrix, and the stress bearing effect of the graphene is improved. Chinese patent publication No. CN 109680188A discloses an alumina layer coated nano aluminum carbide particle reinforced aluminum matrix composite and a preparation method thereof, graphite powder and activated carbon are used as carbon sources to react to obtain an alumina and aluminum carbide composite reinforced aluminum matrix composite, and the method does not give out thermal stability and high temperature mechanical properties of the composite.
Disclosure of Invention
Aiming at the defects in the prior art, the invention aims to provide an in-situ synthesized aluminum carbide reinforced aluminum-based composite material and a preparation method thereof.
According to a first aspect of the present invention, there is provided an in-situ synthesis aluminum carbide reinforced aluminum matrix composite comprising: aluminum powder and graphene powder, wherein the aluminum powder and the graphene powder generate dispersion-distributed aluminum carbide Al with nano scale through in-situ reaction4C3Said nano-scale aluminum carbide Al4C3The aluminum alloy is distributed in the composite material in two forms, wherein one form is that two ends of a rod-shaped appearance grow towards the inner parts of two aluminum crystal grains respectively to nail the two adjacent aluminum crystal grains, and the other form is that the rod-shaped appearance is arranged along a grain boundary in the length direction, so that dislocation and grain boundary migration can be effectively prevented.
Preferably, the graphene powder has a volume fraction of 0.5-2%.
Preferably, the graphene powder is 0.8-2% by volume.
Preferably, the tensile strength of the composite material at room temperature is 200MPa-300MPa, and the hardness reaches 60HV-88 HV.
Preferably, the composite material has a tensile strength of 105MPa to 165MPa and an elongation of about 6% to 10% at a temperature of more than 300 ℃.
According to a second aspect of the present invention, there is provided an in situ synthesis of Al4C3The preparation method of the reinforced aluminum matrix composite material comprises the following steps:
s1: carrying out ball milling mixing on aluminum powder and graphene powder under the protection of argon atmosphere, and carrying out ball milling to obtain uniform mixed powder, wherein the graphene is uniformly dispersed on the surface of the aluminum powder after ball milling, and part of graphene sheet layers can be embedded into an aluminum crystal under the action of ball milling and shearing;
s2: carrying out hot-pressing sintering or spark plasma sintering on the ball-milled mixed powder, wherein the sintering pressure is 50-100MPa and the temperature is 500-;
s3: and extruding or hot rolling the obtained billet at the temperature of 450-550 ℃ to form a compact composite material.
Preferably, the ball milling process adopts a high-energy ball milling method, the ball milling rotating speed is 300-.
Preferably, the graphene powder adopts nano-thickness graphene nanosheets, which is beneficial to controlling Al4C3The dimensions are on the nanometer scale. The graphene powder adopts the graphene nanosheets with the diameter and thickness both in nanometer size, so that the control of Al is facilitated4C3Both length and width are in the nanometer scale.
Compared with the prior art, the invention has at least one of the following beneficial effects:
1) the graphene in the invention has higher tensile strength but poorer wettability with aluminum, and Al is synthesized by graphene powder and aluminum powder in situ4C3The aluminum substrate has orientation relation with the aluminum substrate, and the interface wettability and the interface bonding strength can be further improved. In one aspect of the invention, the Al is in the nanometer scale4C3Effectively pinning the grain boundary migration of the Al matrix, keeping the strength of the Al matrix and simultaneously Al4C3As a hard reinforcing phase, the composite material has higher room temperature strength and high temperature mechanical property due to stress bearing and olorowan effect, and the composite material has wide application prospect in the field of high service temperature conditions such as aerospace and the like.
2) In the invention, no special requirements are made on the purity and the sphere diameter of the Al powder, and the Al powder can be atomized conventionally; the graphene with the nano-scale sheet diameter and the nano-scale sheet thickness is used as an initial carbon source, so that the control of Al is facilitated4C3The dimensions are on the nanometer scale.
3) The high-strength heat-resistant Al is prepared by in-situ synthesis4C3The aluminum-based composite material has higher tensile strength and thermal stability at room temperature, and the high-temperature (300 ℃ and above) tensile strength is superior to that of aluminum alloy reported by most literatures, so that the aluminum-based composite material can meet the service requirements of aerospace materials at different use temperatures.
Drawings
Other features, objects and advantages of the invention will become more apparent upon reading of the detailed description of non-limiting embodiments with reference to the following drawings:
FIG. 1a is a photograph of a low power transmission structure of a composite material according to a preferred embodiment of the present invention;
FIG. 1b is a photograph of a composite high power transmission tissue in accordance with a preferred embodiment of the present invention;
FIG. 1c is a photograph of a composite high power transmission tissue in accordance with a preferred embodiment of the present invention;
FIG. 2 is a drawing curve of an aluminum matrix composite at 300 ℃ in accordance with a preferred embodiment of the present invention;
FIG. 3 shows Al obtained when the graphene volume fraction is 2.5% in an embodiment of the present disclosure4C3An aluminum matrix composite.
Detailed Description
The present invention will be described in detail with reference to specific examples. The following examples will assist those skilled in the art in further understanding the invention, but are not intended to limit the invention in any way. It should be noted that variations and modifications can be made by persons skilled in the art without departing from the spirit of the invention. All falling within the scope of the present invention.
Example 1
This example provides an in situ synthesis of Al4C3The reinforced aluminum-based composite material comprises aluminum powder and graphene powder, wherein the volume fraction of the graphene powder is 0.8%, and the aluminum powder and the graphene powder are subjected to in-situ reaction to generate dispersion-distributed Al with nanoscale4C3Nano-scale of Al4C3The aluminum alloy is distributed in the composite material in two forms, wherein one form is that two ends of a rod-shaped appearance respectively grow towards the insides of two aluminum crystal grains to nail two adjacent aluminum crystal grains, and the other form is that the rod-shaped appearance is arranged along a grain boundary in the length direction of the rod shape, so that dislocation and grain boundary migration can be effectively prevented.
In situ synthesis of Al in the above examples4C3The reinforced aluminum-based composite material can be prepared by the following method, which comprises the following specific steps:
s1: selecting aluminum powder with the sphere diameter of 200 meshes and graphene powder with the sheet diameter of about 1 mu m and the layer thickness of about 10nm as raw materials, wherein the volume fraction of graphene is about 0.8%, mixing the aluminum powder and the graphene powder, performing ball milling at the ball milling rotation speed of 350rpm in the argon protection atmosphere, and obtaining uniform mixed powder after ball milling for 5 hours.
S2: and (3) preserving the heat of the mixed powder obtained in the S1 for 1h at 600 ℃ under the pressure of 100MPa, performing hot-pressing sintering, and performing hot-pressing sintering to obtain a billet with the diameter of 40 mm.
S3: the billet obtained in S2 was subjected to hot extrusion at 450 ℃ to obtain a rod having a diameter of 10 mm.
The composite material obtained in this example had no Al observed at the interface after sintering at 600 ℃4C3However, a small amount of rod-like Al was observed at the interface after extrusion4C3Under the condition, the tensile strength of the composite material at room temperature is about 200MPa, the microhardness is 64HV, and the graphene at the interface is completely converted into Al after heat treatment at 650 ℃ for 1h4C3The rodlike carbide is embedded between two crystal grains to pin the grain boundary migration, and the composite material after heat treatment has the tensile strength of 195MPa at room temperature, the strength retention rate of 97.5 percent, the hardness of 60.4HV and the hardness retention rate of 94.3 percent. The composite material is heated to 300 ℃ and kept warm for half an hour, the high-temperature tensile strength is 115MPa, and the elongation is about 8%.
Example 2
This example provides an in situ synthesis of Al4C3The reinforced aluminum-based composite material comprises aluminum powder and graphene powder, wherein the volume fraction of the graphene powder is 1.5%, and the aluminum powder and the graphene powder are subjected to in-situ reaction to generate dispersion-distributed Al with nanoscale4C3Nano-scale of Al4C3The aluminum alloy is distributed in the composite material in two forms, wherein one form is that two ends of a rod-shaped appearance respectively grow towards the insides of two aluminum crystal grains to nail two adjacent aluminum crystal grains, and the other form is that the rod-shaped appearance is arranged along a grain boundary in the length direction of the rod shape, so that dislocation and grain boundary migration can be effectively prevented.
In situ synthesis of Al in the above examples4C3The reinforced aluminum-based composite material can be prepared by the following method, which comprises the following specific steps:
s1: the preparation method comprises the steps of selecting aluminum powder with the sphere diameter of 200 meshes and graphene powder with the sheet diameter of about 200nm and less than 10 layers as raw materials, wherein the volume fraction of graphene is 1.5%, mixing the aluminum powder and the graphene powder, carrying out ball milling at the ball milling rotation speed of 500rpm in the argon atmosphere, and carrying out ball milling for 8 hours to obtain uniform mixed powder.
S2: and (3) preserving the temperature of the mixed powder obtained in the step (S1) for 10min at 620 ℃ under the pressure of 80MPa, performing SPS sintering (spark plasma sintering), and sintering to obtain a billet with the diameter of 40 mm.
S3: the billet obtained in S2 was subjected to hot extrusion at 500 ℃ to obtain a rod having a diameter of 10 mm.
The interface of the composite material obtained by the embodiment generates a small amount of carbide after being sintered at 620 ℃ at room temperature, and the extruded composite material is subjected to heat treatment at 600 ℃ for 24h, so that graphene completely reacts with an Al matrix to generate Al4C3，Al4C3Has a length of about 100-200nm and a width of about 8-15nm, and is made of nano-sized Al4C3The two aluminum grains are distributed in the composite material in two forms, one is that two ends of the rod-shaped form respectively grow towards the inside of two grains, and two adjacent aluminum grains are nailed, as shown in figure 1 b. Another is a rod-like nano Al which is arranged along the grain boundary in the length direction, and is generated in situ and distributed dispersedly as shown in FIG. 1c4C3Dislocation and grain boundary migration can be effectively prevented at higher temperatures. The composite material obtained under the condition has the tensile strength of 280MPa at room temperature and the hardness of about 75HV, and the tensile strength and the hardness are kept unchanged after heat treatment for 1 hour at 600 ℃, 630 ℃ and 650 ℃. The composite material is heated to 300 ℃ and kept warm for half an hour, the high-temperature tensile strength is 145MPa, and the elongation is about 7.5%.
Compared with the graphene in the embodiment 1, the volume fraction of graphene is increased, the ball milling rotation speed and the ball milling time are properly improved, on one hand, the ball milling time is increased, the dispersion is more uniform, and the interface combination is improved; on the other hand, the volume fraction of the graphene is increased, the volume fraction of the carbide generated by the reaction is correspondingly increased, the volume range of pinning grain boundary migration is enlarged, and the stress bearing effect of the carbide is better and remarkable.
Referring to FIG. 1a, which is a photograph of a low power transmission structure, it can be seen from FIG. 1a that the needle-like carbides are dispersed and distributed at the grain boundary of the aluminum matrix, and the length of the carbides is about 100-200nm and the width is about 10nm, as indicated by the arrows in FIG. 1 a.
Referring to FIG. 2, Al prepared in this example is shown4C3The tensile curve of the aluminum-based composite material at 300 ℃ comprises Al4C3Aluminum matrix composite (Al)4C3The composite material/Al) is different from pure Al in tension, and as can be seen from the figure, the composite material obtained by the in-situ reaction has the tensile strength of 113MPa at 300 ℃ and the tensile strength at high temperature is improved by 126 percent relative to pure aluminum under the same condition.
Example 3
This example provides an in situ synthesis of Al4C3The reinforced aluminum-based composite material comprises aluminum powder and graphene powder, wherein the volume fraction of the graphene powder is 2%, and the aluminum powder and the graphene powder are subjected to in-situ reaction to generate Al with nano-scale in dispersion distribution4C3Nano-scale of Al4C3The aluminum alloy is distributed in the composite material in two forms, wherein one form is that two ends of a rod-shaped appearance respectively grow towards the insides of two aluminum crystal grains to nail two adjacent aluminum crystal grains, and the other form is that the rod-shaped appearance is arranged along a grain boundary in the length direction of the rod shape, so that dislocation and grain boundary migration can be effectively prevented.
In situ synthesis of Al in the above examples4C3The reinforced aluminum-based composite material can be prepared by the following method, which comprises the following specific steps:
s1: selecting aluminum powder with the sphere diameter of 1-2 microns and graphene powder with the sheet diameter of 200-300nm and the number of layers of about 10 as raw materials, wherein the volume fraction of graphene is 2%, mixing the aluminum powder and the graphene powder, performing ball milling at the ball milling speed of 500rpm in an argon atmosphere, and performing ball milling for 12 hours to obtain uniform mixed powder.
S2: and (3) keeping the temperature of the mixed powder for 15min at the pressure of 100MPa and the SPS sintering (spark plasma sintering) temperature of 600 ℃ to obtain a billet with the diameter of 40 mm.
S3: the billet obtained in S2 was subjected to hot extrusion at 500 ℃ to obtain a rod having a diameter of 10 mm.
The further increase of the volume fraction of the graphene enables the room-temperature hardness of the composite material obtained under the condition to be about 85HV, the hardness retention rate is 90 percent and 92 percent after heat treatment for one hour at 600 ℃ and 650 ℃, the room-temperature tensile strength is 290MPa, the composite material is heated to 300 ℃ and kept warm for half an hour, the high-temperature tensile strength is 140-150MPa, and the elongation is 6.5-7.0 percent, and the elongation is slightly reduced relative to that of the embodiment 1 and the embodiment 2 due to the increase of the volume fraction of the reinforcing phase.
Example 4
This example is an in situ synthesis of Al4C3The reinforced aluminum-based composite material comprises aluminum powder and graphene powder, wherein the volume fraction of the graphene powder is 2.5%, and the aluminum powder and the graphene powder are subjected to in-situ reaction to generate dispersion-distributed Al with nanoscale4C3Nano-scale of Al4C3The aluminum alloy is distributed in the composite material in two forms, wherein one form is that two ends of a rod-shaped appearance respectively grow towards the insides of two aluminum crystal grains to nail two adjacent aluminum crystal grains, and the other form is that the rod-shaped appearance is arranged along a grain boundary in the length direction of the rod shape, so that dislocation and grain boundary migration can be effectively prevented.
In situ synthesis of Al in the above examples4C3The reinforced aluminum-based composite material can be prepared by the following method, which comprises the following specific steps:
s1: selecting 100-micron aluminum powder and 500-nm sheet diameter graphene powder with 20-30 layers as raw materials, wherein the volume fraction of graphene is 2.5%, mixing the aluminum powder and the graphene powder, performing ball milling at a ball milling speed of 500rpm in an argon atmosphere, and performing ball milling for 10 hours to obtain uniform mixed powder.
S2: and (3) preserving the temperature of the mixed powder for 1h at 600 ℃ under the pressure of 80MPa, and sintering to obtain a billet with the diameter of 40 mm.
S3: the billet obtained in S2 was subjected to hot extrusion at 500 ℃ to obtain a rod having a diameter of 10 mm.
Because the volume fraction of the graphene is higher, a large amount of carbides appear on the interface of the composite material obtained by the embodiment after sintering at 600 ℃ and extrusion at room temperature, the room-temperature tensile strength of the composite material is 150-170MPa, the high-temperature tensile strength is 80MPa, and the elongation is 5%. In this example, when the reinforcing phase exceeds a certain volume fraction, a large amount of reinforcing phase is deposited at the interface, and instead, cracks are preferentially formed at the agglomerated positions, so that the strength and the plasticity of the composite material are simultaneously reduced, as shown in fig. 3, which is a photograph showing that a large amount of carbides are agglomerated at the interface of the composite material.
Example 5
This example is an in situ synthesis of Al4C3The reinforced aluminum-based composite material comprises aluminum powder and graphene powder, wherein the volume fraction of the graphene powder is 0.5%, and the aluminum powder and the graphene powder are subjected to in-situ reaction to generate dispersion-distributed Al with nanoscale4C3Nano-scale of Al4C3The aluminum alloy is distributed in the composite material in two forms, wherein one form is that two ends of a rod-shaped appearance respectively grow towards the insides of two aluminum crystal grains to nail two adjacent aluminum crystal grains, and the other form is that the rod-shaped appearance is arranged along a grain boundary in the length direction of the rod shape, so that dislocation and grain boundary migration can be effectively prevented.
In situ synthesis of Al in the above examples4C3The reinforced aluminum-based composite material can be prepared by the following method, which comprises the following specific steps:
s1: selecting aluminum powder with the sphere diameter of 5-10 microns and graphene powder with the sheet diameter of 300-500nm and the number of layers of about 10 as raw materials, wherein the volume fraction of the graphene is 0.5%, mixing the aluminum powder and the graphene powder, performing ball milling at the ball milling rotation speed of 450rpm in the argon atmosphere, and performing ball milling for 8 hours to obtain uniform mixed powder.
S2: and (3) preserving the heat of the mixed powder for 1h at 500 ℃ under the pressure of 100MPa, and sintering to obtain a billet with the diameter of 40 mm.
S3: the billet obtained in S2 was subjected to hot extrusion at 450 ℃ to obtain a rod having a diameter of 10 mm.
Because the volume fraction of the graphene is lower and the sintering temperature is lower, no carbide is observed on the interface of the composite material obtained by the embodiment after sintering at 500 ℃ and extrusion at room temperature, the room-temperature tensile strength of the composite material obtained under the condition is about 180MPa, after the composite material is subjected to heat treatment at 630 ℃ and 650 ℃, needle-shaped carbide is observed on the interface of the composite material after the heat treatment, the room-temperature tensile strength of the composite material is 170-200MPa, the strength retention rate is more than 94%, the heat resistance is good, the 300-temperature high-temperature tensile strength is about 95-105MPa, and the elongation is 10%.
In the embodiment, since the volume fraction of graphene is low, the generated carbide cannot completely cover all the grain boundaries of the aluminum matrix, the pinning grain boundary effect is weak relative to the high volume fraction, and the stress bearing of the reinforcing phase and the volume fraction of the reinforcing phase are in positive correlation, the high-temperature tensile strength of the embodiment is low relative to that of the embodiment 1 and the embodiment 2.
The above examples can be integrated to show that the volume fraction of graphene affects the performance of the aluminum matrix composite, when the volume fraction of graphene is 0.5%, the generated carbide cannot completely cover all the grain boundaries of the aluminum matrix, the pinning grain boundary effect is weaker than that of a high volume fraction, and the stress bearing of the enhanced phase and the volume fraction of the enhanced phase are in positive correlation; when the volume fraction of the graphene is 2.5%, and the reinforcing phase exceeds a certain volume fraction, a large amount of reinforcing phases are accumulated on the interface, but cracks are preferentially formed at the position of the aggregation, so that the strength and the plasticity of the composite material are reduced at the same time; therefore, the volume fraction of the graphene is controlled to be 0.8-2%, and the high-performance composite material is more favorably obtained. Meanwhile, the ball milling speed, the ball milling time, the sintering pressure, the sintering temperature and the like have certain influence on the performance of the aluminum matrix composite.
The foregoing description of specific embodiments of the present invention has been presented. It is to be understood that the present invention is not limited to the specific embodiments described above, and that various changes and modifications may be made by one skilled in the art within the scope of the appended claims without departing from the spirit of the invention.

Claims (7)

1. An in-situ synthesis aluminum carbide reinforced aluminum matrix composite material is characterized in that: the aluminum powder and the graphene powder are subjected to in-situ reaction to generate dispersion-distributed aluminum carbide Al with nanoscale4C3The nano-scale aluminum carbide Al4C3Distributed in the composite material in two forms, one of which grows towards the inside of two aluminum crystal grains respectively in a rod-shaped shape at two ends and nails two adjacent aluminum crystal grains, and the other oneThe other one is arranged along the grain boundary in the rod-shaped length direction, and can effectively prevent dislocation and grain boundary migration;
the graphene powder adopts nano-thickness graphene nanosheets, so that aluminum carbide Al can be controlled favorably4C3The size is in the nanometer scale; the volume fraction of the graphene powder is 0.5-2%;
carrying out ball milling mixing on aluminum powder and graphene powder under the protection of argon atmosphere, and carrying out ball milling to obtain uniform mixed powder, wherein the graphene is uniformly dispersed on the surface of the aluminum powder after ball milling, and part of graphene sheet layers can be embedded into an aluminum crystal under the action of ball milling and shearing; and carrying out hot-pressing sintering or spark plasma sintering on the ball-milled mixed powder, wherein the sintering pressure is 50-100MPa and the temperature is 500-630 ℃, and sintering to obtain a billet.
2. The in-situ synthesized aluminum carbide reinforced aluminum-based composite material as claimed in claim 1, wherein: the volume fraction of the graphene powder is 0.8-2%.
3. The in-situ synthesized aluminum carbide reinforced aluminum-based composite material as claimed in claim 1, wherein: the tensile strength of the composite material at room temperature is 200MPa-300MPa, and the hardness reaches 60HV-88 HV.
4. The in-situ synthesized aluminum carbide reinforced aluminum-based composite material as claimed in claim 1, wherein: the composite material has the tensile strength of 105-165 MPa and the elongation of about 6-10% at the temperature of more than 300 ℃.
5. A preparation method for in-situ synthesis of aluminum carbide reinforced aluminum matrix composite is characterized by comprising the following steps: the method comprises the following steps:
s1: carrying out ball milling mixing on aluminum powder and graphene powder under the protection of argon atmosphere, and carrying out ball milling to obtain uniform mixed powder, wherein the graphene is uniformly dispersed on the surface of the aluminum powder after ball milling, and part of graphene sheet layers can be embedded into an aluminum crystal under the action of ball milling and shearing;
s2: carrying out hot-pressing sintering or spark plasma sintering on the ball-milled mixed powder, wherein the sintering pressure is 50-100MPa and the temperature is 500-;
s3: and extruding or hot rolling the obtained billet at the temperature of 450-550 ℃ to form a compact composite material.
6. The method for preparing the aluminum carbide reinforced aluminum matrix composite material synthesized in situ according to claim 5, wherein the method comprises the following steps: the ball milling process adopts a high-energy ball milling method, the ball milling rotating speed is 300-500rpm, and the ball milling time is 5-20 h.
7. The method for preparing the aluminum carbide reinforced aluminum matrix composite material synthesized in situ according to claim 5, wherein the method comprises the following steps: the graphene powder adopts nano-thickness graphene nanosheets, so that aluminum carbide Al can be controlled favorably4C3The dimensions are on the nanometer scale.
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